Note: Descriptions are shown in the official language in which they were submitted.
1 It is known that tool steels and articles made there-
from benefi~ from the standpoint of wear resistance from the pre-
sence of substantial amounts of an MC-type carbide dispersion.
~lowever, as the carbide content is increased, the workability of
the steel is impaired. Consequently, with conventionally melted
and cast alloys of this type a practical limit is placed upon the
total M~-type carbide content
Specifically, tool s-teels and articles made therefrom ~-
are required to have a combination of yield strength to withstand
deformation under the high stresses encountered in service~ wear
resistance to withstand wear during contact with the workpiece,
such as during rolling~ extruding, blanking, punching~ slitting
and the like~ and toug~mess to prevent breaking-away or chipping
of the tool during contact with the workpiece For this purpose
it is known to use tool steels having an alloy-steel matrix with
a dispersion of carbide particles, with the carbide particles
being present for purposes of wear~resistance and the matrix pro-
viding the desired strength and toughness. Consequently~ in
alloys of this type it is accepted that the wear resiætance there-
of is increased with increasing carbide content and particularlyMC-type vanadium carbides. Carbides of this type contribute most
significantly to wear resistance because of their relative hard-
ness~ For this reason, large amounts of MC-type vanadium carbides
are obtained by stoichiometrically balancing the MC-type carbide
former vanadium with carbon. The stoichiometric relationship for
MC-type vanadium carbide formation is 1% vanadium and 0 20~ car-
j¦ bon
~ As recognized, with increases in this car~ide content
; the toughness of the steel is reduced; in addition~ however~ the
toughness and workability are adversely affected by carbide
--1 ~
~L132~
1 segregation which occurs during solidification of ingots or othercastings of the alloy; growth of the carbide particles to an
unduly large size is unavoida~le. Consequently, with conventional
tool steels, the MC-typevanadium carbide content is limited to a
maximum of about 8.2~ by volume.
U.S. Patent 3,746,518 discloses cobalt, iron and nickel
base alloys with a plurality of carbide-forming elements in a
general way but does not discriminate among the various matrix
materials as well as among the various carbide-forming elements
or set an upper limit with respect to any of the carbide-forming
elements~ Evidently, these factors were not considered import-
ant ! In contrast, the present invention deals exclusively with
iron-base alloys and with vanadium as the critical carbide-forming
element and sets critical limits with respect to the vanadium
and vanadium carbide content.
It is accordingly the primary object of this invention
to provide a powder-metallurgy steel article having a high content
of substantially spherical and uniformly distributed MC-type
vanadium carbides, which impart yreatly improved wear resistance
to the article while maintaining toughness and workability at
acceptable levels.
; This and other objects of the invention, as well as a
more complete understanding thereof, may be obtained from the
foll4wing description, specific examples and drawings, in which:
FIGURE 1 is a photomicrograph of a portion of a tool
steel article produced in accordance with the present invention
and showing the characteristic MC-type vanadium carbide formation
in the alloy matrix;
,, .
;: FIGURE 2 is a photomicrograph similar to FIG , 1 , except
with a higher MC-type vanadium carbide content also in accordance
with the invention;
- . ~ - : - .
: . . . .
., .. , . ' ~
~32~4
1 FIGURE 3 iS a photomicro~raph similar to FIGS~ 1 and 2,
except with ~ still higher MC-type vanadium carbide content which
is at the upper, permissible limit of the invention;
FIGUR~ 4 likewise is a photomicrograph similar to FIGS,
1, 2 and 3, except that the MC-type vanadium carbide content
exceeds the upper limit of the invention, and some of these car
bi.des are larger than 15 microns in size, not substantially ~ -
spherical and not uniformly distributed in accordance with the
invention;
FIGURE 5 is a photomicrograph of a portion of a tool
steel article having a composition, and specifically a vanadium
content, i.n accordance with the invention but of an ingot cast
article rather than a powder metallurgy produced article;
FIGURE 6 iS a photomicrograph of a portion of a tool
steel article similar to the article of FIG, 5 but having a higher
vanadium content;
FIGURE 7 is a graph showing the relationship between
impact toughness and MC-type vanadium carbide content;
FIGURE 8 is a graph showing the relationship between
wear resistance and MC-type vanadium carbide content;
FIGURE 9 is a graph showing the effect of austenitizing
treatment on the hardness of a powder metallurgy article-in
accordance with the invention and identified as sample CPM lOV;
and
~ IGURE 10 is a graph showing the effect of tempering
tempexature at a tempering time of 2 + 2 hours on the hardness of
.~ a powder metallurgy article in accordance with the invention and
;: identified as sample CPM lOV~
The term "MC-type vanadium carbide" as used herein
refers to the carbide characterized by the face-centered-cubic
-3-
'
'
~L13L~2~
1 crystal structuxe with "M" representing the carbide-forming
element essentially vanadium; also includes M4C3-type vanadium
carbi.des and includes the partial replacement of carbon by nit-
rogen and/or oxygen to encompass what are termed "carbonitrides"
and "oxycarbonitrides" Although the powder metallurgy article
of this inven-tion is defined herein as containiny su~stantially
all MC-type vanadium carbides, it is understood that other types
of carbides, such.as M6C~ M2C, and M23C6 carbides~ may also be
present in minor amounts, but are not significant from the stand-
point of achieving the objects of the invention
The term "powder metallurgy article" as used herein is
used to designate a compacted prealloyed particle charge that has
been formed by a combination of heat and pressure into a coherent
mass having a density, in final form, in excess of 99% of theor-
etical density; this includes intermediate products such as
billets, blooms~ rod and bar and the like, as well as final pro~
ducts such as tool steel articles including rolls, punches~ dies,
wear plates and the like, which articles may be fa~ricated from
intermediate product forms from the inital prealloyed particle
~o charge
Broadly in the practice of the invention a prealloyed
powder charge is o~tained wherein each particle thereof has an
alloy steel matrix with a uniform dispersion of MC-type vanadium
carbides ~ithin the range of 10 to 18%, preferably l5 to 17% or
13.3 to 17 2% by volume The carbides are of substantially
spherical shape and are uniformly distributed. More specifically
the prealloyed powder from which the powder metallurgy article of
the invention is formed has a metallurgical composition~ in weight
percent, and MC-type vanadium carbide content, in volume percent,
; 30 within the following ranges;
.: .
"
2~
1 Broad Preferred Preferred
Manganese .2 to 1.5 .4 to ,6 ,2 to 1
Silicon 2 max, 1 max. 2 max,
Chromium 1,5 to 6 5 to 5.5 4,5 to 5.5
Molybdenum ,50 to 6 1.15 to 1,4 .80 to 1,7
Sulfur .30 max. .~9 max. .14 max,
Vanadium 6 to 11 9.25 to 10.25 8 to 10.5
Carbon 1.6 to 2.8 2.40 to 2.50 2,2 to 2~6
Iron* Bal. Bal, Bal.
MC-type vanadium ~1~ to 18 ~15 to 17 ~13~3 to 17.2
carbides (per-
cent by volume)
*includes incidental elements and
impurities characteristic of steel-
making practice
The article of the invention is further characterized
by the MC-type vanadium carbides being substantially spherical
and uniformly distributed. The carbon content is balanced with
the vanadium, chromium and molybdenum contents to provide suffic-
ient carbon to permit the powder metallurgy article to be heat
treated to a hardness of at least 56 Rc.
Further with respect to the metallurgical composition
of the prealloyed powder if the manganese content is outside the
upper limit set forth above, the resulting article is difficult to
anneal to the low hardness required for machining purposes. On
"~ the other had if manganese i5 too low there will not ~e sufficient
- manganese present to form the manganese sulfides necessary to pro-
vide adequate machinability. If the silicon exceeds the maximum
limit the hardness of the article will be too high in the annealed
condition for machining. Chromium is required for adequate hard-
`
enability during heat treatment and, in addition, promotes
.
.
.. . . .
-: .:
~3Z5~
1 ele~ated-temperature strength If the chromium content is too
high, this leacls to the formation of high-temperature ferrite or
retention of unduly large amounts of austenite during heat treat- -
ment. The formation of high-temperature ferrite adversely affects
hot-workability, and retained austenite impairs attainment of the
desired high hardness levels during heat treatment. Molybdenum,
like chromium, imparts high temperature strength and hardenability
to the alloy article. Sulfur promotes machinability by providing
for the formation of manganese sulfides. Carbon should be
balanced with vanadium for purposes of forming MC-type vanadium
carbides to provide wear resistance. Also, it is necessary for
adequate matrix hardening that the carbon be present in an amount
to combine with all of the vanadi~n present and additionally be
present for matrix strengthening.
A particle charge of this character may be compacted
by any powder metallurgy technique to the desired product form so
long as such technique does not cause excessive, detrimental
growth and agglomeration of the carbides. It is preferred to use
the well known technique of hot isostatic pressing of an enclosed
charge of prealloyed, atomized powder in an autoclave.
This invention deals with powder-metallurgically pro-
duced alloy steel compositions and powder metallurgy articles
that contain substantially all MC-type vanadium carbides, Further-
more, by controlling the vanadium content and the MC-type vanadium
: carbide content at critical levels a heretofore unobtainable com-
bination of wear resistance and toughness, along with acceptable
grindability is achieved.
The invention is illustrated by the alloys reported in
Table I~ The alloys CPM 6V, CPM llV and CPM 14V were prepared by
3~ ~ making prealloyed powder by induction melting and gas
328~
1 atomization, (2) screening the powder to -40 mesh size ~U S~
Standard), ~3~ placing the powder in 5-1/2 in diameter x 6 in.
high mild steel cans~ (4) outgassing and sealing the cans, (5)
heating the cans to 2140F ana holding at that temperature for
nine hours, (6) consolidating by action of isostatic pressure of
13 2 ksi to essentiall.y full density, and (7) cooling to ambient
temperature. The compacts were then readily hot forged (using
20~0F forging temperature) to 1 in square bars from which var-
ious test specimens were prepared.
~ :
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cq ~
o ~oo ~r ~~I c~ ~ !
i~ ~ ~ ~ ~ , :
O ~ ~ ~ a:) o o u
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,--1 C~ ~ r) ~ o
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il ¢ C~ . . . .
I I Z ~ I ~ ~
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H ~ o O O1~c ~1 oo~ ~o u~
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~; ~:E: X J~ ~ ~ ~ ,.,: '
0 ~ ~ O O -- --
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~:4 ~ C~ 1~ Q
o r~oo ~1 ~ I`;t
E~ 5~a ~ I
æ a~ o , ~ D
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~' ~U~ ~ P ~ X
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Z~
For comparisor purposes, similar compositions identified
as C6V and CllV were induc~ion melted in the form of 100-lb. heats
and teemed into 5-in square molds lined with refractory brick.
These ingots ~.~ere then subjected to forging (using 2000~F neating i
temperature) by the same schedule as had been used on the
corresponding powder metallurgy compacts CPM 6V and CPM llV. The
C6V steel reported in Table I could ~e forged, exercizing
appreciable care, to 3-in. square bar; whereas, the CllV steel I -
I¦ reported in Table I suffered severe cracking on the initial
forging reduction and thus proved to be practically unworkable.
The distinctly superior hot workability of the powder metallurgy
products CPM 6V and CPM llV was conclusively indicated by this
experiment,
The material of CPM lOV was prepared by (1) making
prealloyed powder by induction melting and gas atomization, (2)
screening the powder to -16 mesh size ~u.S, Standardj, (3j piacing
the powder in a 12-3/4-in. diameter 0 D x 60-in. high mild steel
can, (4) outgassing the can, (5) heating the can to 2150F, (6)
consolidating by action of isostatic pressing o~ 12 ksi to
essentially full density, (73 cooling to ambient temperature. The
compact was then (1) heated to 2100F, (2) hot rolled to billet
with 10-1/2 x 3-in. cross section, (3) annealed, (4) conditioned,
(5) heated to 2075F, (6) forged to 8.469 x 1.969-in. cross
section, and (7) machined to 8.015 x 1 765-in cross section.
1~32~
1 The material of CPM 16V was prepared by (1) making pre-
alloyed powder by induction melting and gas atomization, (2)
screening the powder to -20 mesh size (U.S. Standard)~ (3) placing
the powder in a 1 in. diameter I.~. x 4-in. high mild steel can,
(4) outgassing the can, (5) heating the can to 2175 F, and (6)
consolidating by the action of a forging press to essentially full
density.
To obtain an evaluation of the performance character-
istics of the alloys, determinations of the key properties per-
taining to their application in cold work tooling were conducted.These included: U) microstructure, ~2) hardness in the heat
treated condi~ion as a measure of strength, (3) bend fracture
strength as well as impact value as measures of toughness and (4)
wear rate in the cross-cylinder wear test as a measure of wear
resistance.
The characteristics of the MC-type vanadium carbides
in articles of Steels CPM 6V, CPM 10~, CPM llV, CPM 14V, C6V and
CllV are illustrated in FIGS. 1, 2, 3, 4, 5 and 6, respectively.
By application of a known special selective etching technique
(successive application of picral and Murakami's reagentsl)~ the
MC--type vanadium carbides are made to appear as white particles
on a dark background (containing all other microconstituents).
It is clearly evident that the MC-type vanadium carbide particles
,
Picral consists of 5 grams picric acid in 100 ml ethyl alcohol;
Murakami's reagent consists of 10 grams potassium ferricyanide
and 7 grams of sodium hydroxide in 100 ml of water.
~10-
3L$~2~
1 are uniformly distributeZ, small in size, and essentially spher-
ical in shape in Steels CPM 6V, CPM lOV and CPM llV of FIGS. 1,
2 and 3, respectively, In these steels, at least 90% of the MC-
type vanadium carbides are less than 3 microns in size and none
àre substantially greater than 15 microns in si.ze in any.dimen-
sion On the other hand, CPM 14V of FIG, 4 and the ingot cast
Steels C6V and CllV of FIGS, 5 and 6, respectively, are character-
ized by the presence of distinctly larger angularly shaped, e,g,
non-spherical, MC-typ~ vanadium carbides~ These large angularly
shaped carbides appear in clusters throughout the microstructure
of the article and result in a nonuniform MC-type vanadium carbide
distribution. With regard to the characteristics of the MC-type
vanadium carbides, Steels CPM 6V, CPM lOV and CPM llV are
: illustrative of the MC~type vanadium carbide appearance of articles
within the scope of this invention; whereas, those in Steels
CPM 14V, C6V and CllV are characteristic of articles outside the
scope of the invention,
In addition to the MC-type vanadium carbide size~ shape
and distribution, this invention emphasizes ~he importance of the
amount of the MC-type vanadium carbides present in the articles.
The amount of MC-type vanadium carbides present in Steels CPM 6V,
CPM lQV, CPM llV, CPM 14V~ C6V and CllV was computed based.on the
well accepted fact that the vanadium content of the steel.is
present in the form of MC or M4C3 type carbides, where M is
essentially all vanadium and the vanadium/carbon xatio is 5:1, in
weight percent. It is understood that in alloys of this type
tungsten is usually present as a "tramp" element, although it is
not :intentionally added for any purpose For the ~urther
; materials used for comparison purposes, the volume percentages for
AISI A7 and D7 were computed on t~e same basis as for the
l, experimental steels using the nominal vanadium contents of 4.75
. and 4 0 weight percent, respectively, as the vanadium contents of
the steels. For AISI M2 and ~4 high speed steels, the volume
percentages of ~IC-type vanadium carbide contents were taken from r
l technical publication by Kayser and Cohen in Metal Progress, June
¦ 1952, pages 79-85.
; I Hardness is a measure of the ability of the steel to
resist deformation during service in cold-work or warm-work tool-
ing A minimum hardness of Rc 56 is usually required The result s
presented in Table II were obtained on hardness testing in
accordance with ASTM E18-67 Standard after a heat treatment
; consisting of austenitizing at 1750F for 1 hour, oil quenching
and tempering at 500F for 2+2 hours.
TABLE II
MC-Type Vanadium
DescriptionType ofCarbide Content Hardness
: of SteelM~nufacture(Vol. %) (Rc)
CPM 6V P/M 10.5 62
C6V Ingot Cast 10.2 56
CPM llV P/M 17.7 63
CllV Ingot Cast 18,2 50
. . .
l2
. ~ :~
~ ~ 3Z~ ~
Superiority of the produc. produced in accordance with
the .invention (CP~I 6V and CP~ llV) over the ingot-cast product
(C6V and CllV) in heat trea~ing response is clearly evident.
, Specimens of CPM lOV have been subjected to a wide
, variety of heat treatments conslsting of austenitizing, cooling
I~ and tempering. The results of austenitizing are presented in
',¦ FIG. 9 wherein the time-at-temperature relationship was as
follows:
Temperature (F) Time (Minutes)
I
1 1850 60
1950 60
2100 15 '
2150 10
2200 4
2300 4
ThP r~s1t1 tc o f tl~mnerl'ng treatm-en-t *re shown in FT~; 1 n
From these FIGS. it is evident that the heat treated hardness of
56 Rc can be achieved for articles of the invention in the
austenitized and tempered condition over a broad treatment range.
Bend fracture strength is a measure of toughness. The
determination of this property is made at the smbient temperature
. on specimens 1/4 in. sq. x 1-7/8-in. long using three-point load-
ing with a 1-1/2-in. support span and applying a bending rate of
O.l in. per minute. The bend fracture strength is the stress
which causes fracturing of the specimen. It is calculated using
the following formula:
2~ :
S = 3 PL
2bh~
where
S is t~e bend fracture strength (psi or ksi)
~ P is the load required to cause fracture (lb.)
i L is the support span (in.)
,I b is the specimen width (i~)
?l h is the specimen height ~in.)
¦~ The results reported in Table III were obtained in :
¦ testing specimens that had been heat treated by austenitizing at
1750~F for 1 hour, oil quenching and tempering at 500F for 2~2
: hours.
TABLE III
I Designation Type of Bend Fracture
; I of Steel Manufacture Strength (ksi)
15 l CPM 6V P/M 700
: ¦ - C6V Ingot Cast 420 ?
: The superiority of the powder-metallurgy prepared product in
. accordance with the invention is clearly evident, -;
~"
. Impact toughness tests were conducted on Charpy-type
, 20 specimens at room temperature in accordance with the ASTM E23-72
procedure on specimens having a notch radius of 1/2 in. The
resul reported Ln Table IV were obtained,
~ .
"
': . /~
' ' = _~
~3Z~
TABLE I~J
~; ~C-Type Vanadium Impact
DesignationT~pe of Carbide Content Hardness Value
of Steel~fanufacture (VOL, C/~ - (RC) (ft-lb~
I~
CP~I 6V P/M 10.5 62 35
CPM lOV P/M 16.2 63 18
CPM llV P/M 17.7 63 16
C6V Ingot Cast 10 2 56 11
¦I CllV Ingot Cast 18.2 50 1.5
¦1 AISI Ingot Cast 8.0 61 11
Type A7*
AISI Ingot Cast 9.0 63 12
Type M4*
_ . .
*from commercial stock
From Table IV it may be seen that the articles of this invention,
even with substantially greater carbide content, were superior in
toughness to the conventional c~mmercial cold-work or warm-work
tool materials in their optimum heat treated condition for cold-
work tooling application.
The toughness data reported in Table IV are graphically
presented in FIG. 7. These data show that with MC-type vanadium
carbide contents exceeding about 18% by volume the toughness of
product in accordance with the invention decreases to the tough-
ness level achieved conventionally and thus this advantage of the
invention is lost.
For evaluation of wear resistance, the crossed-cylinder
wear test was used. In this test, a cylindrical specimen (5/8 in.
/5' .
:,
, . , , : . . . :
diamete~) o~ the respective cold-worl.~ or warm-work tool material
and a cylindrical specimen (1/2 in. diameter) or tungsten carbide
(with 6/o cobalt binder) are positioned perpendicularly to one
another. A filteen-pound load is applied through ~eight on a
lever arm. Then the tungsten carbide cylinder specimen is
rotated at a speed of 667 revolutions per minute. No lubrication
il is applied. As the test progresses, a wear spot develops on the
i specimen of the tool material. From time to time, the extent o~
Il wear is determined by measuring the depth of the wear spot on the
ll specimen and converting it into wear volume by aid of a relation-
ship specifically derived for this purpose. The wear resistance,
or the reciprocal of the wear rate, is then computed according to
the following formula:
Wear resistance ' wear ra~e~ v = -~ v
where
v a the wear volume, (in.3)
L = the applied l~d; (1h )
s = the sliding distance, (in.)
d = the diameter of the tungsten carbide cylinder, (in.)
and N = the number of revolutions made by the tungsten
carbide cylinder, (rpm)
This test has provided excellent correlations with wear
situations encountered in practice.
Applying this wear test to specimens of this invention,
as well as to some currently widely used highly wear-resistant
cold-work or warm-work tooling materials from commercial stock,
the data reported in Table V resulted:
/G~
;~ ~
~ ::
:~ ' " ~
T~.~LE V
Designation Hard- MC-Type ~lanadium Wear
of Type of ness Carbide Content Resistance
Steel ~nufacture (~c) (Vol. /~ (101 Psi)
5, CPM llV P/~ 63 17.7 66
,i CPM lOV P/~l 63 16.2 90
i! CPM 6V P/M 62 10.5 20
AISI A7~ Ingot Cast 61 8.0 15
¦ AISI D7* Ingot Cast 61 6.7 7
10AISI M4* Ingot Cast 63 9.0 11
AISI M~* Ingot Cast 64 3.1 6
*from commercial stock .
The superiority of the alloys of this invention with
.` regard to wear resistance is clearly evident from the reported
data, Specifically, as shown in Table V and FIG 8, the wear
resistance of the CPM 10 sample is significantly ~uperior tn tk~
wear resistance of the CPM 11 sample, which has a higher MC-type
vanadium carbide content and thus would be expected to have higher
wear resistance. As may be seen from FIG. 8 a minimum MC-type
vanadium carbide content of 10% by volume is needed to attain a
significant advantage in wear resistance over conventional
; material. Therefore, a minimum MC-type vanadium carbide content
is established by these data for articles in accordance with the
invention. The upper limit with respect to the ~IC-type vanadium
` 25 carbide content is established by the finding that the relatively
-:~ _~7
. ~ ~ I
z~
large-sized ~IC-t~pe vanadium carbldes that are presen~ in the
micrc)structu z of ste~ls having Janadi~m contents of about 11% or
higher or ~!C-type vanadiu~ carbide contents of about 18% or higher
.;
by ~olume have a deleterious effect on the grindability of the
steel Grindability is an important consideratlon because
, grinding is often used in the manufacture of tools and other
wear-resistant articles from steels of this type. The effect of
the MC-type vanadium carbide size on grindability is evident from ¦
~I the results of the following experiment conducted on samples from
¦ Steels CPM lOV and CPM 16V. These two steels have essentially the
same chemical compositions except for their vanadium and carbon
contents, and their MC-type vanadium carbide contents; CPM lOV is
within the scope of this invention, whereas CPM 16V is not.
Specimens of both steels were rough machined and heat
treated by austenitizing at 2150F for 4 minutes, oil quenching,
and tempering at 1000F for 2f~ hours. After this treatment, the
hardness of the CPM lOV steel was 63.5 Rc and that of the CPM 16V
steel w~s ~4.5 Rc. The specimens were then finish machined to the
final size: 1.234 in. (length) by 0.398 in. (width) by 0.344 in.
(thickness), -
The grindability evaluation was done by use of a Norton
horizontal-spindle surface grinding machine equipped with a
; reciprocating table and magnetic chuck. The grinding conditions
~ used were as follows:
- ` ~
~3~
.
Cross feed - .008 in.
Cross speed - 92 ft./min.
Down feed - .0010 in./pass
Grinding ~heel - 4-A-54-H-10-V-FM
I Grinding wheel speed - 2000 rpm
Coolant - CX-30S
!I Specimen surface area _ .49 in 2
l subjected to grinding
ll Before each test, the specimen thickness was measured
~ with a micrometer. After ten passes ~with a grinding wheel down
feed of .0010 in./pass), the specimen thickness was remeasured and
the change in specimen thickness calculated, The difference
between the down feed of the grinding wheel in 10 passes (10 x
,0010 = .010 in.) and the measured resulting change in the
speci~en thickness indicates the wear of the grinding wheel in
terms of its radius. The smaller the wear of the grinding wheel,
the better is the grindability of the workpiece material.
Three tests were run on each of the specimens GPM lOV
~ and~CPM 16V. The grinding wheel was dressed before each test,
By using the procedure described above, the following ~ `
resul were obtained:
/f
' ,, :
.`
.
' .' ~ ' ~
1 Challge in Specimen Thickness Average Grinding
Steel (in.) Wheel Wear*
~in.)
Average
l~V .~097, .0096, .0098 .0097 .0003
16V .0091, .0093, .0091 .0092 .0008
*Determined as the difference between the down feed of grinding
wheel in 10 passes ~.0100 in.) and the average change in specimen
thickness in 10 passes.
It is evident from these results that the 16V specimen
which is outside the scope of the invention from the standpoint
of the MC-type vanadium carbide content being above the upper
limit of the invention, exhibits unsatisfactory grindability and
significantly inferior to the grindability of the lOV specimen
that is within the scope of the invention.
Bars ~0.756 in. diameter) of Steel CPM llV were manu-
factured into "cold extrusion punches" and subjected to actual
service as punches involved in the production of spark plug shells
from AISI 1008 steel. The performance of punches is determined
by the number of shells produced before undue wear necessitates
their replacement. The results reported in TABLE VI were obtained.
TABLE VI
MC-Type Vanadium Average No.
Extrusion Carbide Content of Parts Produced
Punch Material lVol. %) Per Puncb (in 1000)
CPM llV 17.7 42
AISI M4* 9.0 22
::
*from commercial stock
The performance advantage of the alloy of this invention,
CPM llV, over the AISI Type M4 high-speed steel is clearly evident.
As another illustration, a punch made of CPM lOV steel
was used as a tool for punching slots into iron-oxide-coated tags.
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'Z~
1 Forty million tags were produced without wear or buildup on the
tool. In comparison, the same tool made from AISI D7 (containing
4% vanadium or 6.7 volume percent of vanadium carbide) failed
after producing 8,000,000 to 12,000,000 tags.
As a further trial application, a punch was made of
CPM lOV and used in punching slots in 0.015 inch-thick copper-
beryllium alloy strip for producing electronic parts. While the
same punch made of AISI D2 cold-work tool steel heat treated to
Rc 60 to 62 hardness is normally worn out after producing 75,000
parts and one made of AISI M4 high speed steel heat treated to
Rc 64 hardness shows some wear after producing 200~000 parts~ the
punch made of CPM lOV heat treated to RC60 hardness showed no
wear after producing 200,000 parts.
The articles of this invention are fabricable into
tooling components without undue difficulties. They can be
annealed to 250 to 300 Brinell hardness and machined, ground~
drilled, etc., as needed to form the desired tool shape,
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